KR100467719B1 - Method of producing ferritic stainless steel sheets having softning, anti-ridging property and excellent spinning formability - Google Patents

Method of producing ferritic stainless steel sheets having softning, anti-ridging property and excellent spinning formability Download PDF

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KR100467719B1
KR100467719B1 KR10-2000-0074743A KR20000074743A KR100467719B1 KR 100467719 B1 KR100467719 B1 KR 100467719B1 KR 20000074743 A KR20000074743 A KR 20000074743A KR 100467719 B1 KR100467719 B1 KR 100467719B1
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stainless steel
ferritic stainless
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KR20020045322A (en
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유도열
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주식회사 포스코
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

본 발명은 연질이며, 리징 저항성 및 스피닝 가공성이 우수한 페라이트계 스테인리스강 및 그 제조방법에 관한 것이다. 중량%로 C: 0.035% 이하, Si: 0.3% 이하, Mn: 1% 이하, P: 0.035% 이하, S: 0.03% 이하, Cr: 15 ~ 17%, Mo: 0.03% 이하, N: 0.035% 이하, Cu: 0.4% 이하, Al: 0.005% 이하, 나머지 Fe 및 불가피하게 첨가되는 불순물로 조성되고, 또한 강도 인자인 H(%)=4(C%+N%) + Si%가 0.5% 이하를 만족하고, 하기 계산식으로부터 소재의max(%)값이 32% 이상, Ac1 온도가 820℃ 이하, 이론 항복강도(YS, Kg/㎟)가 32(Kg/㎟) 이하를 만족하는 페라이트계 스테인리스강과, 상기 페라이트계 스테인리스강을 1200 ~ 1250℃로 가열하는 단계와, 마무리 압연온도를 950℃ 이하, 권취온도를 750℃ 이하로 열간압연하는 단계와, 상기 열간압연판을 830 ~ 850℃에서 4시간 이상 상소둔하는 단계와, 상기 열간압연소둔판을 냉간압연율 70 ~ 95%로 1회 냉간압연하는 단계와, 냉간압연후 840 ~ 870℃ 범위에서 냉간압연소둔처리하는 것을 특징으로 하는 연질이며, 리징성 및 스피닝 가공성이 우수한 페라이트계 스테인리스강 제조 방법을 제공한다.The present invention relates to a ferritic stainless steel that is soft and has excellent leaching resistance and spinning processability and a method of manufacturing the same. By weight% C: 0.035% or less, Si: 0.3% or less, Mn: 1% or less, P: 0.035% or less, S: 0.03% or less, Cr: 15-17%, Mo: 0.03% or less, N: 0.035% Or less, Cu: 0.4% or less, Al: 0.005% or less, remaining Fe and inevitably added impurities, and the strength factor H (%) = 4 (C% + N%) + Si% is 0.5% or less Satisfies the The ferritic stainless steel having a max (%) value of 32% or more, an Ac1 temperature of 820 ° C or lower, and a theoretical yield strength (YS, Kg / mm 2) of 32 (Kg / mm 2) or less, and the ferritic stainless steel 1200 Heating to ˜1250 ° C., hot rolling a finishing rolling temperature of 950 ° C. or lower, and winding temperature of 750 ° C. or lower, and subjecting the hot rolled plate to 830 to 850 ° C. for at least 4 hours; Cold rolling the hot rolled annealing plate at a cold rolling rate of 70 to 95% once, and cold rolling annealing in the range of 840 to 870 ° C after cold rolling, and has excellent leaching property and spinning processability. Provided is a method for producing a stainless steel.

Max(%)=420C+470N+10Mn+18 Cu +23Ni-11.5Si-11.5Cr-12Mo-49Ti-52Al+180, Max (%) = 420C + 470N + 10Mn + 18 Cu + 23Ni-11.5Si-11.5Cr-12Mo-49Ti-52Al + 180,

Ac1(℃) = (Cr+1.72Mo+2.09Si+4.86Nb+1.77Ti+2.14Al-7.14C-8N-3.28Ni-1.89Mn-1.02Cu)x35+310,Ac1 (° C.) = (Cr + 1.72Mo + 2.09Si + 4.86Nb + 1.77Ti + 2.14Al-7.14C-8N-3.28Ni-1.89Mn-1.02Cu) x35 + 310,

이론YS(Kg/mm2)=47.6+92.4Si+11Mn+801P+9.48Cr+68.5Ti+35.1Al+939(C+N)/9.8)Theory YS (Kg / mm 2 ) = 47.6 + 92.4Si + 11Mn + 801P + 9.48Cr + 68.5Ti + 35.1Al + 939 (C + N) /9.8)

Description

리징 저항성 및 스피닝 가공성이 우수한 페라이트계 스테인리스강 및 그 제조 방법{Method of producing ferritic stainless steel sheets having softning, anti-ridging property and excellent spinning formability}Method of producing ferritic stainless steel sheets having softning, anti-ridging property and excellent spinning formability

본 발명은 연질이며, 리징 저항성 및 스피닝 가공성이 우수한 페라이트계 스테인리스강 및 그 제조방법에 관한 것이다.The present invention relates to a ferritic stainless steel that is soft and has excellent leaching resistance and spinning processability and a method of manufacturing the same.

일반적으로 주방 양식기 용도로 사용되는 STS430 페라이트계 스테인리스강은 강도가 높은 경우에 스피닝 가공시 크랙발생율이 높고, 또한 스프링 백(spring back)이 심하여 형상동결성이 나쁘다. 또한 소재의 리징(ridging) 저항성이 나쁜 경우 성형후 연마 과정에서 리징 흔적이 잔존하는 등 문제점이 많이 발생한다.In general, STS430 ferritic stainless steel, which is used for kitchenware, has a high cracking rate during spinning when the strength is high, and also has a bad spring back, resulting in poor shape freezing. In addition, when the ridging resistance of the material is bad, a lot of problems occur, such as the remaining traces in the polishing process after molding.

이러한 문제점을 해결하기 위한 종래의 제안들중 일본 특개평10-280047호에서는 내 로핑(ropping)성이 우수한 페라이트계 스테인리스강판 제조 방법으로 Al, B, Ta, Nb, V 등이 첨가된 강에서p를 15 ~ 35%로 조절하고, 열간압연 , 냉간압연조건 및 조질압연율을 적정화하여 로핑성을 개선하는 것을 특징으로 하지만, 본 발명강과 조성 및 제조조건이 다르다. 그리고 한국 특허 등록번호 10-0263365(공개특허번호 1997-0015775호)에서는 면내이방성이 작고 내 리징성이 우수한 페라이트계 스테인레스강판 및 그 제조방법에 관한 것으로 강의 조성, 압연조건, 소둔조건을 적정화하여 특유의 집합조직이 발달 되도록 제어하는 방법이지만 집합조직 제어가 용이하지 않는 문제점과 본 발명강과 화학조성이 다른 B 및 Ti가 다량 첨가된 강이다. 또한 이들 특허는 스피닝성 개선에 대한 방법이 제시되지 않았다.In Japanese Patent Application Laid-open No. Hei 10-280047 to solve such a problem, a method of manufacturing ferritic stainless steel sheet having excellent roping resistance is used in steel to which Al, B, Ta, Nb, and V are added. Although p is adjusted to 15 to 35%, hot rolling, cold rolling conditions, and temper rolling ratio are optimized to improve roping property, but the composition and manufacturing conditions of the present invention are different. In addition, Korean Patent Registration No. 10-0263365 (Published Patent No. 1997-0015775) relates to a ferritic stainless steel sheet having a low in-plane anisotropy and excellent ridging resistance, and a method of manufacturing the same. Although the method of controlling the development of the texture of the structure is not easy to control the texture of the steel and the steel of the present invention and the chemical composition of the B and Ti is a large amount is added. In addition, these patents do not suggest a method for improving spinning property.

이에 본 발명자는 상기한 문제점들을 해결하고자 페라이트계 스테인리스강의 리징 저항성과 스피닝 가공성을 개선시키기 위하여 실험을 행하고 그 결과를 근거하여 본 발명을 제안하게 되었다.In order to solve the above problems, the present inventors have conducted experiments to improve the ridging resistance and spinning processability of ferritic stainless steel and proposed the present invention based on the results.

본 발명은 각종 계산식을 사용하여 합금성분계 범위를 적정하게 설정하고, 일정 수준의 제품특성을 갖도록 제조조건을 제어함으로써 연질이며, 리징 저항성과 스피닝 가공성을 개선시킨 페라이트계 스테인리스강 및 그 제조하는 방법을 제공하고자 하는데 그 목적이 있다.The present invention relates to a ferritic stainless steel which is soft by setting the alloy component range appropriately using various calculation formulas and controlling the manufacturing conditions to have a certain level of product characteristics, and has improved leasing resistance and spinning processability, and a method of manufacturing the same. The purpose is to provide.

본 발명은 페라이트계 스테인리스강 및 그 제조방법에 있어서,In the present invention, a ferritic stainless steel and a method of manufacturing the same,

중량 %로 C: 0.035% 이하, Si: 0.3% 이하, Mn: 1% 이하, P: 0.035% 이하, S: 0.03% 이하, Cr: 15 ~ 17%, Mo: 0.03% 이하, N: 0.035% 이하, Cu: 0.4% 이하, Al: 0.005% 이하, 나머지 Fe 및 불가피하게 첨가되는 불순물로 조성되고,By weight% C: 0.035% or less, Si: 0.3% or less, Mn: 1% or less, P: 0.035% or less, S: 0.03% or less, Cr: 15-17%, Mo: 0.03% or less, N: 0.035% Cu: 0.4% or less, Al: 0.005% or less, remaining Fe and inevitably added impurities,

또한 강도 인자인 H(%)=4(C%+N%) + Si%가 0.5% 이하를 만족하고, 하기 계산식으로부터 소재의max(%)값이 32% 이상, Ac1 온도가 820℃ 이하, 이론 항복강도(YS; Kg/㎟)가 32(Kg/㎟) 이하를 만족하는 페라이트계 스테인리스강과,In addition, the strength factor H (%) = 4 (C% + N%) + Si% satisfies 0.5% or less, and from the following formula a ferritic stainless steel having a max (%) value of 32% or more, an Ac1 temperature of 820 ° C or less, and a theoretical yield strength (YS; Kg / mm 2) of 32 (Kg / mm 2) or less,

상기 페라이트계 스테인리스강을 1250 ~ 1200℃로 가열하는 단계와, 마무리 압연온도를 950℃ 이하, 권취온도를 750℃ 이하로 열간압연하는 단계와, 상기 열간압연판을 830 ~ 850℃에서 4시간 이상 상소둔하는 단계와, 상기 열간압연소둔판을 냉간압연율 70 ~ 95%로 1회 냉간압연하는 단계와, 냉간압연후 840 ~ 870℃ 범위에서 냉간압연소둔처리하는 것을 특징으로 하는 연질이며, 리징성 및 스피닝 가공성이 우수한 페라이트계 스테인리스강 제조 방법을 제공한다.Heating the ferritic stainless steel to 1250 to 1200 ° C., hot rolling a finish rolling temperature of 950 ° C. or lower, and a winding temperature of 750 ° C. or lower, and hot-rolling the plate at 830 to 850 ° C. for 4 hours or more. The cold annealing step of the step of annealing, the step of cold rolling the hot rolled annealing plate at a cold rolling rate of 70 ~ 95% once, and cold rolling annealing in the range of 840 ~ 870 ℃ after cold rolling Provided is a method for producing ferritic stainless steel having excellent resistance to spinning and spinning.

* H(%) =4(C%+N%)+Si% Max(%) = 420C + 470N + 10Mn + 18Cu - 11.5Si - 11.5Cr - 12Mo - 52Al + 180;Ac1(℃) = (Cr + 1.72Mo + 2.09Si + 2.14Al - 7.14C - 8N - 1.89Mn - 1.02Cu) x 35 + 310;YS(Kg/㎟) = 47.6 + 92.4Si + 11Mn + 801P + 9.48Cr + 35.1Al + 939(C + N)/9.8; * H (%) = 4 (C% + N%) + Si% Max (%) = 420C + 470N + 10Mn + 18Cu-11.5Si-11.5Cr-12Mo-52Al + 180; Ac1 (℃) = (Cr + 1.72Mo + 2.09Si + 2.14Al-7.14C-8N-1.89Mn- 1.02Cu) x 35 + 310; YS (Kg / mm 2) = 47.6 + 92.4 Si + 11Mn + 801P + 9.48Cr + 35.1Al + 939 (C + N) /9.8;

이하 본 발명강에 대한 한정한 이유를 설명하면 다음과 같다.Hereinafter, the limited reason for the inventive steel will be described.

상기 C 및 N는 탄질화물 형성원소로 침입형으로 존재하면 강도가 높아지고, 내식성 및 스피닝 가공성을 저하시키기 때문에 낮게 유지할수록 바람직하므로 그 함량은 C의 경우는 0.035% 이하, N은 0.035% 이하로 한정한다.When C and N are in the intrusion type as carbonitride-forming elements, the strength is high, and since corrosion resistance and spinning processability are lowered, the lower the C and N, the more preferable it is. do.

Si는 페라이트 형성원소로 함량 증가시 페라이트 상의 안정성이 높아지게 되고 내산화성이 향상되나 0.3% 이상 첨가하면 경도, 항복강도, 인장강도를 높이고 연신율을 저하시키기 때문에 스피닝 가공성에 불리하여 0.3% 이하로 한정한다.Si is a ferrite forming element which increases the stability of ferrite phase and improves oxidation resistance, but when added more than 0.3%, the hardness, yield strength, tensile strength and elongation are lowered. .

Mn은 함량이 높아지면 MnS를 용출하여 내공식성을 저하시키기 때문에 1.0% 이하로 한정한다.Mn is limited to 1.0% or less because the content of Mn elutes MnS and lowers pitting resistance.

P 및 S는 MnS등 개재물을 형성하여 내식성 및 열간가공성을 저해하므로 가능한 낮게 관리하는 것이 좋기 때문에 P :0.035% 이하, S : 0.03% 이하로 한정한다.Since P and S form inclusions such as MnS to inhibit corrosion resistance and hot workability, P and S should be kept as low as possible, so they are limited to P: 0.035% or less and S: 0.03% or less.

Cr은 함량이 15% 이하로 너무 낮으면 내식성이 저하하고 함량이 17% 이상이면 내식성은 향상이 되나 강도가 높고 연신율이 낮아 스피닝 가공성이 저하하기 때문에 그 함량은 15 ~ 17%로 한정한다.Cr content is less than 15%, the corrosion resistance is lowered, if the content is 17% or more, the corrosion resistance is improved, but the strength is high and the elongation is low, so the spinning processability is lowered, the content is limited to 15 ~ 17%.

Mo는 함량이 증가하면 내식성은 현저하게 향상시키지만 강도를 높여 성형성이 나빠진다. 따라서 내식성 및 성형성을 고려하여 Mo 함량을 0.03% 이하로 한정한다.As the Mo content increases, the corrosion resistance is remarkably improved, but the moldability is worsened by increasing the strength. Therefore, considering the corrosion resistance and moldability, the Mo content is limited to 0.03% or less.

Al은 탈산제로 첨가되는 원소로 다량 첨가하면 표면결함을 발생시키기 때문에 0.005% 이하로 한정한다.Al is limited to 0.005% or less because an element added as a deoxidizer causes a large amount of surface defects.

Cu는 감마상 생성원소로 많이 첨가하면max(%)가 증가하지만 합금철 투입량 증가에 의한 제조원가 상승하고, 열간가공성이 저하하여 열간압연시 표면결함을 유발하기 때문에 Cu는 0.4% 이하로 한정한다.Cu is added as a gamma phase generating element Although the max (%) increases, the manufacturing cost increases due to the increased ferroalloy amount, and the hot workability decreases, causing surface defects during hot rolling. Therefore, Cu is limited to 0.4% or less.

다음은 본 발명강의 계산식 값의 한정이유에 대해 설명하면Next, the reason for limitation of the formula value of the present invention steel

강도인자인 H(%)의 한정 이유에 대해 설명하면, 페라이트계 스테인레스강의 강도에 가장 크게 작용하는 원소인 C, N , Si은 연질화를 목적으로 강도 인자인 H(%)=4(C%+N%)+Si%가 0.5% 초과이면 소재의 경도 및 강도가 상승하여 스피닝시 형상 동결성이 나빠진다. 따라서 형상 동결성 개선을 위해 연질화가 필요함으로 H(%)는 0.5% 이하를 만족하는 범위내 합금조성으로 한정한다.Explaining the reason for limiting the strength factor H (%), the elements C, N, and Si, which have the greatest effect on the strength of ferritic stainless steel, have the strength factor H (%) = 4 (C%) for the purpose of soft nitriding. If + N%) + Si% is more than 0.5%, the hardness and strength of the material increase, resulting in poor shape freezing during spinning. Therefore, soft nitriding is required to improve shape freezing, so H (%) is limited to an alloy composition within a range satisfying 0.5% or less.

소재의 화학성분을 계산식에 대입하여 구한max(%)가 32% 미만 이면 리징성이 현저하게 나빠지기 때문에max(%)는 32% 이상이 되는 합금조성으로 한정한다.Calculated by substituting the chemical composition of the material If max (%) is less than 32%, the ridging property is significantly worse. max (%) is limited to an alloy composition of 32% or more.

소재의 화학성분을 계산식에 대입하여 구한 Ac1 온도의 범위에 대해 설명하면, 페라이트계 스테인레스강에 있어서 통상의 열연소둔 및 냉간압연소둔온도는 소재의 Ac1 온도 직하에서 열처리하는 것이 연질 및 연신율 개선에 유리하다. 그러나 통상 열간압연소둔은 상소둔 설비(BAF)에서 소둔온도가 높아지면 내부덮개(inner cover)에 변형이 발생하여 소둔온도를 높일 수가 없다. 따라서 Ac1 온도가 820℃ 이하로 낮을수록 통상의 상소둔 설비에서 내부덮개변형이 발생하지 않는 온도 범위내에서 소둔하면 재질을 개선시킬수가 있다. 따라서 소재의 Ac1 온도가 820℃ 보다 높은 소재는 통상 열연소둔 온도인 820℃에서 4시간 소둔처리하면 재결정이 불충분하게 일어나 경질로 연신율이 저하하는 문제점이 발생하기 때문에 계산식으로 구한 소재의 Ac1 온도는 820℃ 이하를 만족시키는 합금조성으로 한정한다.Referring to the range of Ac1 temperature obtained by substituting the chemical composition of the material into the equation, the normal hot and cold rolling annealing temperatures of ferritic stainless steel are advantageous for improving the softness and elongation. Do. However, in general, hot rolling annealing may increase the annealing temperature due to deformation of the inner cover when the annealing temperature is increased in a BAF. Therefore, when the Ac1 temperature is lower than 820 ° C., the material can be improved by annealing within a temperature range in which the inner cover deformation does not occur in a normal annealing apparatus. Therefore, if the Ac1 temperature of the material is higher than 820 ℃, annealing treatment for 4 hours at 820 ℃, which is a hot-rolling annealing temperature, will result in insufficient recrystallization. It is limited to the alloy composition which satisfies below C.

연질화를 통한 스피닝성 개선을 위해 소재의 화학성분을 계산식에 대입하여구한 이론 항복강도(YS, Kg/mm2)는 32(Kg/mm2) 이하가 되는 합금조성으로 한정한다.The theoretical yield strength (YS, Kg / mm 2 ) obtained by substituting the chemical composition of the material for the improvement of spinning property through soft nitriding is limited to the alloy composition which is 32 (Kg / mm 2 ) or less.

이하, 본 발명의 제조조건 한정 이유에 대해 설명하면 다음과 같다.Hereinafter, the reason for limitation in manufacturing conditions of the present invention will be described.

상기와 같이 조성된 강을 1250℃ 초과하여 가열하면 열간압연시 표면결함이 많이 생기고, 1200℃ 미만으로 가열하면 압연온도가 낮아 열간압연중 스티킹 등 표면결함이 다량 발생하기 때문에 열간압연을 위한 최적 슬라브 가열온도는 1200 ~ 1250℃ 범위내로 한정한다.When the steel composition is heated above 1250 ℃, many surface defects occur during hot rolling, and when it is heated below 1200 ℃, a large number of surface defects such as sticking during hot rolling occur due to low rolling temperature. The slab heating temperature is limited in the range of 1200-1250 ° C.

열간압연 마무리 압연온도가 950℃ 초과하고, 권취온도가 750℃ 초과하면 열간압연중 내부에 축적된 내부 변형 축적 에너지가 작아 열간압연판 소둔시 재결정이 충분하게 일어나지 않기 때문에 마무리 압연온도는 950℃ 이하, 권취온도는 750℃ 이하로 한정한다.If the hot rolling finish rolling temperature exceeds 950 ℃ and the coiling temperature exceeds 750 ℃, the internal strain accumulation energy accumulated inside during hot rolling is small, so that recrystallization does not occur sufficiently during annealing of the hot rolled finish. , The coiling temperature is limited to 750 ℃ or less.

열간압연판 소둔온도는 820℃ 이하에서는 재결정이 불충분하게 일어나 연신율이 낮고, 강도가 높아 스피닝 가공성이 저하한다. 그리고 850℃ 온도 이상에서는 고온에서상이 생성되어, 냉각중 마르텐사이트생성으로 연신율 및 스피닝 가공성이 현저하게 저하하기 때문에 열간압연 소둔온도는 재결정이 충분하게 일어나 연신율이 높은 820 ~850℃ 범위로 하고, 소둔시간은 코일 내,외부가 충분하게 재결정이 일어나는 시간인 4시간 이상으로 한정한다.In the hot-rolled sheet annealing temperature, recrystallization is insufficient at 820 ° C. or lower, resulting in low elongation, high strength, and poor spinning workability. And at high temperatures above 850 ℃ As the phase is formed and the elongation and spinning workability significantly decrease due to martensite formation during cooling, the hot rolling annealing temperature is sufficient to recrystallize and the elongation is high in the range of 820 to 850 ° C. It is limited to 4 hours or more, which is the time for recrystallization to occur.

상소둔한 열간압연 소둔판을 냉간압연율 70 ~ 95% 냉간압연하는 이유로는 냉간압연율이 적정 범위를 벗어나면 냉간압연 소둔판의 Δr 값이 +0.1을 초과하여 스피닝 작업시 압연방향으로는 높은 귀가 발생하고, 압연방향과 직각방향으로는 낮은 귀가 발생하여 최종 제품 가공후 커링(curling) 작업시 귀가 낮은 부위에서는 소재 폭이 부족하여 커링작업 불량이 발생하기 때문에 스피닝용 소재는 Δr 값이 +0.1 이하로 냉간압연시 냉간압연율이 70 ~ 95% 범위내로 단압연하여 제조하는 방법으로 한정한다. 2회 압연 및 2회 소둔처리재인 재압연재는 Δr 값이 +0.1을 초과하여 높아지고, 또한 단압연재인 경우도 냉간압연율이 70% ~ 95 범위를 벗어나면 Δr 값이 +0.1을 초과하여 변화되기 때문에 단압연재로 냉간압연율이 70 ~ 95% 범위내로 한정한다.The reason for cold rolling 70 ~ 95% of cold rolled annealing plate is that hot rolled annealing plate is out of an appropriate range. Δr value of cold rolled annealing plate exceeds +0.1. Spinning material has a Δr value of +0.1 or less because low ears are generated in the rolling direction and in a direction perpendicular to the rolling direction. It is limited to the method of manufacturing by cold rolling within the range of 70 ~ 95% cold rolling at the time of cold rolling. The re-rolled material, which is twice rolled and twice-annealed material, has a higher Δr value over +0.1. Also, in the case of short rolled material, if the cold rolling rate is out of the range of 70% ~ 95, the Δr value changes over +0.1. For this reason, cold rolling is limited to 70 to 95% of short rolling material.

냉간압연소둔온도에 대해 설명하면 일반적으로 냉간압연소둔 공정에서는 열간압연소둔에 비해 라인 스피드가 빠르기 때문에 소재의 Ac1 온도가 상승한다. 따라서 냉간압연 소둔온도가 840℃ 미만에서는 재결정이 불충분하게 일어나 연신율이 낮고, 강도가 높아 스피닝 가공성이 저하된다. 그리고 870℃ 초과에서는 고온에서상이 생성되어, 냉각중 마르텐사이트생성으로 연신율 및 스피닝 가공성이 현저하게 저하하기 때문에 냉간압연소둔온도는 재결정이 충분하게 일어나 연신율이 높은 840 ~870℃ 범위로 한정한다.In the case of the cold rolling annealing temperature, in general, in the cold rolling annealing process, since the line speed is faster than that of the hot rolling annealing, the temperature of the material Ac1 increases. Therefore, when cold rolling annealing temperature is less than 840 degreeC, recrystallization may become inadequate, low elongation is high, high strength, and the spinning workability falls. And at high temperatures above 870 ° C. Because the phase is formed and the martensite is formed during cooling, the elongation and spinning workability are significantly reduced, so the cold rolling annealing temperature is limited to a range of 840 to 870 ° C. where the elongation is high enough to cause recrystallization.

이하, 실시예를 통하여 본 발명을 보다 구체적으로 설명한다.Hereinafter, the present invention will be described in more detail with reference to Examples.

표 1은 본 발명의 실시예 소재로서의 화학성분을 나타내고, 표 2는 표 1의 화학성분으로 본 발명의 계산식에 의해 구한 각각의 값을 나타내었다. 상기와 같이 조성된 페라이트계 스테인레스강을 50Kg 진공유도 용해로에서 용해하여 인고트를 제조하였다. 이와같이 제조된 주괴를 1240℃에서 120분간 가열하고, 940℃의 마무리온도에서 열간압연하여 3.2mm 두께의 열간압연판을 제조하고, 820℃에서 4.5시간 상소둔(BAF)처리후 산세처리 하였다.Table 1 shows chemical components as examples of the present invention, and Table 2 shows the respective values obtained by the formula of the present invention with the chemical components of Table 1. An ingot was prepared by dissolving the ferritic stainless steel prepared as described above in a 50 Kg vacuum induction melting furnace. The ingot thus prepared was heated at 1240 ° C. for 120 minutes, hot rolled at a finishing temperature of 940 ° C. to produce a 3.2 mm thick hot rolled plate, and subjected to pickling treatment at 820 ° C. for 4.5 hours after annealing (BAF).

상기 열간압연 소둔판을 85%의 냉간압연율로 냉간압연하여 0.5mmt를 제조하고 820 ~ 870℃범위로 냉간압연소둔온도를 변화시켜 냉간압연소둔후 공냉하는 1단 압연재와 비교재로 3.2mmt 열간압연 소둔판을 1.0mmt(냉간압연율 68%)로 냉간압연후 850℃에서 냉간압연 소둔처리하고, 다시 0.5mmt(냉간압연율 50%)로 냉간압연후 다시 냉간압연 소둔처리하는 2단 압연재를 각각 산세한 다음 1% 냉간압연율로 조질압연하여 각종 특성 평가용 시편을 제조하였다.The hot rolled annealing plate is cold rolled at a cold rolling rate of 85% to prepare 0.5mmt, and the cold rolling annealing temperature is varied in the range of 820 ~ 870 ° C, followed by cold rolling annealing and 3.2mmt as a comparative material. The cold rolled annealing plate is cold rolled to 1.0mmt (cold rolling rate 68%), then cold rolled annealed at 850 ℃, cold rolled to 0.5mmt (50% cold) and then cold rolled annealed again. After the pickling of each of the soft materials and rough rolling at 1% cold rolling rate to prepare a variety of specimens for the evaluation of properties.

인장시험용 시편은 JIS 13B로 가공하여 시험하고, 리징 높이 측정은 JIS 5호로 압연방향과 평행한 방향으로 인장시편을 가공하여 15% 인장후 표면조도기로 리징(ridging) 높이를 측정하여 최대 높이값으로 리징 높이를 나타내었다.Tensile test specimens were tested by JIS 13B, and the ridging height was measured by JIS 5 in the direction parallel to the rolling direction. After the 15% tension, the ridging height was measured using a surface roughness to obtain the maximum height. The ridging height is shown.

스피닝 가공성 평가는 자동 스피닝 기계를 이용하여 0.5mmt 소재를 사용하여 직경이 293mm인 블랭크를 각 시편별로 10개씩 펀칭하여 원추형 가공품의 직경이 225mm, 높이가 95mm 인 제품으로 스피닝 가공하여 성형품 톱부위에 10mm 커링 작업후에 내부 및 외부를 연마하여 크랙발생, 연신 불량과 리징 흔적 잔존 유무 및 커링성 불량율을 조사하였다.Spinning workability evaluation was performed by using an automatic spinning machine, punching 10 blanks of 293mm diameter for each specimen by using 0.5mmt material and spinning the product into 225mm diameter and 95mm height cones. After the curing operation, the inside and the outside were polished to investigate the occurrence of cracking, elongation defects, the presence of ridging traces, and the poor curability.

(wt%)(wt%) 구분division NoNo CC SiSi MnMn PP SS CrCr MoMo CuCu AlAl NN 발명재Invention 1One 0.030.03 0.240.24 0.510.51 0.020.02 0.010.01 16.1516.15 0.030.03 0.030.03 0.0030.003 0.030.03 22 0.0300.030 0.250.25 0.40.4 0.020.02 0.020.02 16.1916.19 0.030.03 0.040.04 0.0030.003 0.030.03 비교재Comparative material 33 0.0410.041 0.390.39 0.4650.465 0.190.19 0.0190.019 16.5016.50 0.0130.013 0.0310.031 0.0040.004 0.040.04 44 0.0370.037 0.2670.267 0.4410.441 0.0230.023 0.0060.006 16.1716.17 0.0110.011 0.0310.031 0.0050.005 0.0340.034 55 0.0470.047 0.390.39 0.390.39 0.0210.021 0.0020.002 8.168.16 0.010.01 0.0200.020 0.0030.003 0.04880.0488 66 0.0500.050 0.310.31 0.270.27 0.0180.018 0.010.01 16.5816.58 0.050.05 0.010.01 0.0050.005 0.0380.038 77 0.0610.061 0.30.3 0.610.61 0.0250.025 0.0020.002 16.416.4 0.030.03 0.040.04 0.0040.004 0.030.03

구분division NoNo 4(C%+N%)+Si%4 (C% + N%) + Si% r Max(%)r Max (%) Acl(℃)Acl (℃) 이론 Y.S (Kg/㎟)Theory Y.S (Kg / ㎡) 발명재Invention 1One 0.48(%)0.48 (%) 32.732.7 811.7811.7 30.7130.71 22 0.49(%)0.49 (%) 35.935.9 803.9803.9 30.6630.66 비교재Comparative material 33 0.714(%)0.714 (%) 31.231.2 839.2839.2 34.3434.34 44 0.551(%)0.551 (%) 31.131.1 825.5825.5 32.2132.21 55 0.7732(%)0.7732 (%) 40.340.3 831.7831.7 35.5135.51 66 0.662(%)0.662 (%) 28.228.2 864.5864.5 34.0434.04 77 0.664(%)0.664 (%) 43.343.3 795.7795.7 34.8634.86

각 강종별 제품 특성을 평가한 결과는 표 3에 나타난 바와 같이 강도 지수인 H(%)=4(C+N)+Si 가 0.5% 이하이고,max(%)가 32% 이상이며, Ac1 온도가 820℃ 이하, 이론 항복강도(YS)가 32Kg/㎟ 이하인 본 발명강은 상기 조건을 만족시키지 않는 비교강에 비해 경도 및 항복강도는 낮고, 연질로 연신율은 높고, 리징성도 비교적 양호한 특성을 보이고 있다.As a result of evaluating the product characteristics of each steel type, the strength index of H (%) = 4 (C + N) + Si is 0.5% or less, as shown in Table 3, The steel of the present invention having max (%) of 32% or more, Ac1 temperature of 820 ° C. or lower, and theoretical yield strength (YS) of 32 Kg / mm 2 or lower of the present invention has lower hardness and yield strength than the comparative steel that does not satisfy the above conditions. The elongation is high and the ridging property is relatively good.

구분division NoNo 경도 (Hv)Hardness (Hv) 항복강도(Kg/㎟)Yield strength (Kg / ㎡) 연신율 El(%)Elongation El (%) 리징 높이(㎛)Leasing Height (μm) 발명재Invention 1One 142.7142.7 31.231.2 28.828.8 21.921.9 22 143.0143.0 31.331.3 28.728.7 22.022.0 비교재Comparative material 33 158.9158.9 34.034.0 26.526.5 23.123.1 44 151.1151.1 33.533.5 28.528.5 22.622.6 55 158.7158.7 34.534.5 26.626.6 19.719.7 66 155.4155.4 33.433.4 25.725.7 25.625.6 77 156.2156.2 34.334.3 28.028.0 28.128.1

또한 실물 스피닝 시험 결과는 나타낸 표 4에 나타난 바와 같이 본 발명강은 비교강에 비해 연질이고, 리징 저항성도 양호하기 때문에 스피닝후 형상동결성도 우수하고, 스피닝시 크랙발생이 나타나지 않았으며, 연마후 리징 흔적 잔존이 없고, 냉간압연시 단연압으로 제조하였기 때문에 본 발명강은 커링성도 양호하였다는 것을 나타낸다.In addition, as shown in Table 4, the actual spinning test results show that the inventive steel is softer than the comparative steel and has better ridging resistance. Since there was no trace | survival remainder and it manufactured by cold rolling at cold rolling, it shows that the steel of this invention also had good curability.

구분division NoNo 스피닝후형상동결성Post-Spinning Shape Freezing 스피닝시 크랙발생율 (%)Cracking Rate at Spinning (%) 연마후 리징 흔적 잔존율($)Rising trace residual rate after grinding ($) 스피닝 가공후 커링성Curing property after spinning 냉간압연조건Cold Rolling Condition 발명재Invention 1One 양호Good 00 00 양호Good 단압연Short rolling 22 양호Good 00 00 양호Good ″″ 비교재Comparative material 33 불량Bad 5050 00 양호Good ″″ 44 불량Bad 3030 00 양호Good ″″ 55 불량Bad 2020 00 양호Good ″″ 66 불량Bad 100100 100100 양호Good ″″ 77 불량Bad 2525 100100 불량Bad 재압연Reroll

시편Psalter 냉연소둔 온도(℃)Cold Annealing Temperature (℃) 820820 830830 840840 850850 870870 발명강 no.1Invention Steel no.1 연신율(%)Elongation (%) 2929 3131 31.531.5 3232 3333

표 5에 나타낸 바와 같이 상기 본 발명강 1을 냉간압연소둔온도 840 ~ 870℃범위내로 소둔하는 경우 연신율이 향상되는 것을 볼 수 있다. 이것은 본 발명의 냉간압연소둔온도 840 ~ 870℃범위내에서 소둔함으로써 재결정이 충분하게 일어나 연신율이 높아지고 스피닝 가공성이 좋아지는 것이다.As shown in Table 5, when the present invention steel 1 is annealed in the cold rolling annealing temperature range of 840 ~ 870 ℃ it can be seen that the elongation is improved. This is annealing in the cold rolling annealing temperature of 840 ~ 870 ℃ range of the present invention is sufficient to recrystallize, the elongation is high and the spinning workability is improved.

본 발명의 계산식을 사용하여 합금성분계 범위를 적정하게 설정하고, 일정 수준의 제품특성을 갖도록 제조조건을 제어함으로써 페라이트계 스테인리스강에 대한 리징 저항성과 스피닝 가공성을 개선시키는 효과를 가진다.By using the formula of the present invention, the alloy component range is appropriately set, and manufacturing conditions are controlled to have a certain level of product characteristics, thereby improving leasing resistance and spinning processability for ferritic stainless steels.

Claims (2)

페라이트계 스테인리스강에 있어서,In ferritic stainless steel, 중량%로 C: 0.035% 이하, Si: 0.3% 이하, Mn: 1% 이하, P: 0.035% 이하, S: 0.03% 이하, Cr: 15 ~ 17%, Mo: 0.03% 이하, N: 0.035% 이하, Cu: 0.4% 이하, Al: 0.005% 이하, 나머지 Fe 및 불가피하게 첨가되는 불순물로 조성되고,By weight% C: 0.035% or less, Si: 0.3% or less, Mn: 1% or less, P: 0.035% or less, S: 0.03% or less, Cr: 15-17%, Mo: 0.03% or less, N: 0.035% Cu: 0.4% or less, Al: 0.005% or less, remaining Fe and inevitably added impurities, 강도인자(H)는 0.5% 이하, 소재의max은 32% 이상, Ac1 온도는 820℃ 이하, 이론항복강도(YS)는 32(Kg/㎟) 이하이고, 여기에서The strength factor (H) is 0.5% or less of the material max is 32% or more, Ac1 temperature is 820 ° C or less, theoretical yield strength (YS) is 32 (Kg / mm 2) or less, where H(%) = 4(C%+N%)+Si%;H (%) = 4 (C% + N%) + Si%; Max(%) = 420C + 470N + 10Mn + 18Cu - 11.5Si - 11.5Cr - 12Mo - 52Al + 180; Max (%) = 420C + 470N + 10Mn + 18Cu-11.5Si-11.5Cr-12Mo-52Al + 180; Ac1(℃) = (Cr + 1.72Mo + 2.09Si + 2.14Al - 7.14C - 8N - 1.89Mn - 1.02Cu) x 35 + 310;Ac 1 (° C.) = (Cr + 1.72Mo + 2.09Si + 2.14Al-7.14C-8N-1.89Mn-1.02Cu) x 35 + 310; YS(Kg/㎟) = 47.6 + 92.4Si + 11Mn + 801P + 9.48Cr + 35.1Al + 939(C + N)/9.8;YS (Kg / mm 2) = 47.6 + 92.4 Si + 11 Mn + 801 P + 9.48 Cr + 35.1 Al + 939 (C + N) /9.8; 인 것을 특징으로 하는 연질이며, 리징성 및 스피닝 가공성이 우수한 페라이트계 스테인리스강.A ferritic stainless steel characterized by being soft and excellent in ridging and spinning processability. 중량%로 C: 0.035% 이하, Si: 0.3% 이하, Mn: 1% 이하, P: 0.035% 이하, S: 0.03% 이하, Cr: 15 ~ 17%, Mo: 0.03% 이하, N: 0.035% 이하, Cu: 0.4% 이하, Al: 0.005% 이하, 나머지 Fe 및 불가피하게 첨가되는 불순물로 조성되고, 강도인자(H)는 0.5% 이하, 소재의max은 32% 이상, Ac1 온도는 820℃ 이하, 이론항복강도(YS)는 32(Kg/㎟) 이하인 페라이트계 스테인리스강을 제조하는 방법에 있어서,By weight% C: 0.035% or less, Si: 0.3% or less, Mn: 1% or less, P: 0.035% or less, S: 0.03% or less, Cr: 15-17%, Mo: 0.03% or less, N: 0.035% Cu: 0.4% or less, Al: 0.005% or less, remaining Fe and inevitably added impurities, the strength factor (H) is 0.5% or less, In the method for producing a ferritic stainless steel having a max of 32% or more, Ac1 temperature of 820 ℃ or less, theoretical yield strength (YS) of 32 (Kg / mm2) or less, 상기 조성을 갖는 슬라브를 1200 ~ 1250℃로 가열하는 단계와;Heating the slab having the composition to 1200 to 1250 ° C .; 마무리 압연온도 950℃ 이하의 조건에서 열간압연하는 단계와;Hot rolling under the condition of a finish rolling temperature of 950 ° C. or less; 750℃ 이하의 온도에서 권취하여 열연코일을 준비하는 단계와;Preparing a hot rolled coil by winding at a temperature of 750 ° C. or less; 상기 열연코일을 830 ~ 850℃에서 4시간 이상 상소둔하는 단계와;Annealing the hot rolled coil at 830 to 850 ° C. for at least 4 hours; 상기 열연소둔판을 냉간압연율 70 ~ 95%로 1회 냉간압연하는 단계와;Cold rolling the hot rolled annealing plate once at a cold rolling rate of 70 to 95%; 냉간압연후 840 ~ 870℃ 범위에서 냉간압연 소둔처리하는 것을 특징으로 하는 연질이며, 리징성 및 스피닝 가공성이 우수한 페라이트계 스테인리스강 제조 방법.A method for producing ferritic stainless steel, characterized in that the cold rolling annealing treatment in the range of 840 ~ 870 ℃ after cold rolling, excellent ridging and spinning processability.
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